Duplex Stainless Steel 3rd Edition (1)

7/27/2019 Duplex Stainless Steel 3rd Edition (1)

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www.imoa.info

Practical Guidelines forthe Fabrication ofDuplex Stainless Steels


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The International Molybdenum Association (IMOA) has madeevery effort to ensure that the information presented is technicallycorrect. However, IMOA does not represent or warrant theaccuracy of the information contained in this handbook or itssuitability for any general or specic use. The reader is advisedthat the material contained herein is for information purposes

only; it is not intended as a substitute for any persons procedures,and should not be used or relied upon for any specic or generalapplication without rst obtaining competent advice. IMOA,its members, staff and consultants specically disclaim any andall liability or responsibility of any kind for loss, damage, orinjury resulting from the use of the information contained in thispublication. ASTMs and EN international specificationswere used predominantly in this publication; however, materialspecications may vary among countries.

Practical Guidelines for the Fabricationof Duplex Stainless Steel

Third edition 2014 IMOA 19992014

ISBN 978-1-907470-09-7

Published by the International MolybdenumAssociation (IMOA), London, [email protected]

Prepared by TMR Stainless, Pittsburgh, PA, USA

Designed by circa drei, Munich, Germany

Acknowledgement:IMOA is grateful to the International Stainless Steel Forum andEuro Inox for their support and review of this handbook.We furthermore thank the following companies for their detailed

feedback and contributions: Acerinox, Allegheny Ludlum, Aperam,Aquatech, ArcelorMittal, Baosteel, Columbus Stainless,JSL Limited, Nippon Yakin Kogyo, North American Stainless,Outokumpu Stainless, Sandvik, Swagelok, and Yieh UnitedSteel Corporation.

Cover photo: Meads Reach, Temple Quai, Bristol, UK. www.m-tec.uk.com (fabricator), www.photo-genics.com (photo)


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Contents

1 Introduction 4

2 History of duplex stainless steels 5

3 Chemical composition and role of

alloying elements 8

3.1 Chemical composition of duplex stainless steels 83.2 The role of the alloying elements in duplex

stainless steels 8

4 Metallurgy of duplex stainless steels 10

4.1 Austenite-ferrite phase balance 104.2 Precipitates 11

5 Corrosion resistance 14

5.1 Resistance to acids 145.2 Resistance to caustics 155.3 Pitting and crevice corrosion resistance 155.4 Stress corrosion cracking resistance 17

6 End user specications and quality control 20

6.1 Standard testing requirements 206.1.1 Chemical composition 206.1.2 Solution annealing and quenching 206.2 Special testing requirements 21

6.2.1 Tensile and hardness tests 216.2.2 Bend tests 226.2.3 Impact testing and metallographic

examination for detrimental phases 226.2.4 Phase balance as determined by

metallography or magnetic measurements 236.2.5 Corrosion testing 246.2.6 Production welding and inspection 25

7 Mechanical properties 26

8 Physical properties 29

9 Cutting 319.1 Sawing 319.2 Shearing 319.3 Slitting 319.4 Punching 319.5 Plasma and laser cutting 31

10 Forming 32

10.1 Hot-forming 3210.1.1 Solution annealing 3310.2 Warm forming 3410.3 Cold forming 34

10.4 Press forming 3510.5 Spinforming 35

11 Machining duplex stainless steels 36

11.1 General guidelines for machining duplexstainless steels 36

11.2 Turning and facing 3711.3 Face milling with cemented carbides 3811.4 Twist drilling with high-speed steel drills 39

12 Welding duplex stainless steels 40

12.1 General welding guidelines 4012.1.1 Differences between duplex and austenitic

stainless steels 4012.1.2 Selection of starting material 4012.1.3 Cleaning before welding 40

12.1.4 Joint design 4012.1.5 Preheating 4212.1.6 Heat input and interpass temperature 4212.1.7 Postweld heat treatment 4212.1.8 Desired phase balance 4212.1.9 Dissimilar metal welds 4312.2 Welding procedure qualications 4412.3 Welding methods 4412.3.1 Gas tungsten arc welding (GTAW/TIG) 4412.3.2 Gas metal arc welding (GMAW/MIG) 4612.3.3 Flux core wire arc welding (FCW) 4812.3.4 Shielded metal arc welding

(SMAW/stick electrode) 4412.3.5 Submerged arc welding (SAW) 5012.3.6 Weld overlay electro-slag welding (ESW) 5012.3.7 Electron beam and laser welding 5112.3.8 Resistance welding 51

13 Other joining techniques 52

13.1 Joint preparation 5213.2 Adhesives 5213.3 Soldering 5213.4 Brazing 52

14 Post-fabrication cleanup 53

14.1 Crayon marks, paint, dirt, oil 5314.2 Embedded iron 5314.3 Weld spatter, weld discoloration, ux, slag,

arc strikes 54

15 Duplex stainless steel applications 55

Suggested additional reading 58

References 61

Appendix 1:

Duplex stainless steel designations and

product names 62

Appendix 2:Summary of specications 64


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Duplex stainless steels are a family ofgrades combining good corrosionresistance with high strength and ease offabrication. Their physical propertiesare between those of the austenitic andferritic stainless steels but tend to becloser to those of the ferritics and tocarbon steel. The chloride pitting and

crevice corrosion resistance of theduplex stainless steels are a function ofchromium, molybdenum, tungsten, andnitrogen content. They may be similar tothose of Type 316 or range above thatof the sea water stainless steels such asthe 6% Mo austenitic stainless steels.All duplex stainless steels have chloride

stress corrosion cracking resistancesignicantly greater than that of the 300-series austenitic stainless steels. Theyall provide signicantly greater strengththan the austenitic grades while exhibitinggood ductility and toughness.

There are many similarities in the fabrica-tion of austenitic and duplex stainlesssteels but there are important differences.

The high alloy content and the highstrength of the duplex grades require somechanges in fabrication practice. Thismanual is for fabricators and for end userswith fabrication responsibility. It presents,in a single source, practical informationfor the successful fabrication of duplexstainless steels. This publication assumesthe reader already has experiencewith the fabrication of stainless steels;therefore, it provides data comparing theproperties and fabrication practices ofduplex stainless steels to those of the300-series austenitic stainless steels andof carbon steel.

We hope this brochure will give the readerboth an understanding of the fabricationof structures and components made fromduplex stainless steel, and knowledgethat fabrication of duplex stainless steelsis different but not difficult.

1 Introduction

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Duplex stainless steel bridge in Stockholm, Sweden. Outokumpu


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2 History of duplex stainless steels

Duplex stainless steels, meaning thosewith a mixed microstructure of aboutequal proportions of austenite and ferrite,have existed for nearly 80 years. Theearly grades were alloys of chromium,nickel, and molybdenum. The rst wroughtduplex stainless steels were produced inSweden in 1930 and were used in thesulte paper industry. These grades weredeveloped to reduce the intergranular

corrosion problems in the early, high-carbon austenitic stainless steels. Duplexcastings were produced in Finland in1930, and a patent was granted in Francein 1936 for the forerunner of what wouldeventually be known as Uranus 50. AISIType 329 became well established afterWorld War II and was used extensivelyfor heat exchanger tubing in nitric acidservice. One of the rst duplex gradesdeveloped specifically for improvedresistance to chloride stress corrosioncracking (SCC) was 3RE60. In subsequentyears, both wrought and cast duplexgrades have been used for a variety ofprocess industry applications includingvessels, heat exchangers and pumps.

These rst-generation duplex stainlesssteels provided good performancecharacteristics but had limitations in theas-welded condit ion. The heat-affectedzone (HAZ) of welds had low toughnessbecause of excessive ferrite, andsignificantly lower corrosion resistance

than that of the base metal. In 1968 theinvention of the stainless steel reningprocess, argon oxygen decarburization(AOD), opened the possibility of abroad spectrum of new stainless steels.Among the advances made possible withthe AOD was the deliberate addition ofnitrogen as an alloying element. Nitrogenalloying of duplex stainless steels makespossible HAZ toughness and corrosionresistance approaching that of the basemetal in the as-welded condition. With

increased austenite stability, nitrogen

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also reduces the rate at which detrimentalintermetallic phases form.

The second-generation duplex stainlesssteels are dened by their nitrogen alloy-ing. This new commercial development,which began in the late 1970s, coincidedwith the development of offshore gasand oil elds in the North Sea and thedemand for stainless steels with excellent

chloride corrosion resistance, goodfabricability, and high strength. 2205became the workhorse of the second-generation duplex grades and was usedextensively for gas gathering line pipeand process applications on offshore plat-forms. The high strength of these steelsallowed for reduced wall thickness andreduced weight on the platforms and pro-vided considerable incentive for their use.

Like the austenitic stainless steels, the

duplex stainless steels are a familyof grades ranging in their corrosion per-formance depending on the alloy content.The development of duplex stainlesssteels has continued, and modern duplexstainless steels have been divided intove groups in this brochure, according totheir corrosion resistance. Other ways togroup these steels have been proposed,but no consensus has been reached onthe denition of these groups.

Lean duplex without deliberate Mo

addition, such as 2304; Molybdenum-containing lean duplex,

such as S32003; Standard duplex with around 22% Cr

and 3% Mo, such as 2205, the work-horse grade accounting for nearly 60%of duplex use;

Super duplex with approximately 25%Cr and 3% Mo, with PREN of 40 to 45,such as 2507;

Hyper duplex with higher Cr and Mocontents than super duplex grades

and PREN above 45, such as S32707.

The resistance of a stainless steel tolocalized corrosion is strongly related toits alloy content. The primary elementsthat contribute to the pitting corrosionresistance are Cr, Mo, and N. W, althoughnot commonly used, is about half aseffective on a weight percent basis as Mo.An empirical relationship called thePitting Resistance Equivalent Number(PREN) has been developed to relate a

stainless steels composition to its relativepitting resistance in chloride containingsolutions. The PREN relationship foraustenitic and duplex stainless steels isgiven as follows:

* PREN

= P' R&"$& E"& N,#&

= C + 3.3(M + 0.5!) + 16N

where Cr, Mo, W, and N represent thechromium , molybdenum, tungsten, andnitrogen contents of the alloy, respectively,in weight %.

Table 1 lists the chemical compositionsand typical PREN range of the second-generation wrought duplex stainlesssteels and of the cast duplex stainlesssteels. The rst-generation duplex gradesand the most common austenitic stain-less steels are included for comparison.

Note: Each stainless steel referenced by

name or by industry designation in the textmay be found in Table 1 or Appendix 1.


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Table 1: Chemical composition (weight %) and PREN range of wrought and cast duplex stainless steels*(austenitic grades shown for comparison)

Grade UNS No. EN No. C Cr Ni Mo N Mn Cu W PREN

Wrought duplex stainless steels

First-generation duplex grades

329 S32900 1.4460 0.08 23.028.0 2.55.0 1.02.0 1.00 3031

S31500 1.4424 0.03 18.019.0 4.35.2 2.53.0 0.050.10 2829

S32404 0.04 20.522.5 5.58.5 2.03.0 0.20 2.00 1.002.00 2930

Second-generation duplex grades

Lean duplex

S32001 1.4482 0.03 19.521.5 1.003.00 0.6 0.050.17 4.006.00 1.00 2123

S32101 1.4162 0.04 21.022.0 1.351.70 0.10.8 0.200.25 4.006.00 0.100.80 2527

S32202 1.4062 0.03 21.524.0 1.002.80 0.45 0.180.26 2.00 2528

2304 S32304 1.4362 0.03 21.524.5 3.05.5 0.050.60 0.050.20 2.50 0.050.60 2528

S82011 0.03 20.523.5 1.02.0 0.11.0 0.150.27 2.003.00 0.50 2527

S82012 1.4635 0.05 19.020.5 0.81.5 0.100.60 0.160.26 2.004.00 1.00 2426

S82122 0.03 20.521.5 1.52.5 0.60 0.150.20 2.004.00 0.501.50 2426

1.4655 0.03 22.024.0 3.55.5 0.10.6 0.050.20 2.00 1.003.00 2527

1.4669 0.045 21.524.0 1.03.0 0.5 0.120.20 1.003.00 1.603.00 2527

Molybdenum-containing lean duplex

S32003 0.03 19.522.5 3.04.0 1.502.00 0.140.20 2.00 3031

S81921 0.03 19.022.0 2.04.0 1.002.00 0.140.20 2.004.00 2728

S82031 1.4637 0.05 19.022.0 2.04.0 0.601.40 0.140.24 2.50 1.00 2728

S82121 0.035 21.023.0 2.04.0 0.301.30 0.150.25 1.002.5 0.201.20 2728

S82441 1.4662 0.03 23.025.0 3.04.5 1.002.00 0.200.30 2.504.00 0.100.80 3334

Standard duplex

2205 S31803 1.4462 0.03 21.023.0 4.56.5 2.53.5 0.080.20 2.00 3335

2205 S32205 1.4462 0.03 22.023.0 4.56.5 3.03.5 0.140.20 2.00 3536

S32950 0.03 26.029.0 3.55.2 1.02.5 0.150.35 2.00 3638

S32808 0.03 27.027.9 7.08.2 0.81.2 0.300.40 1.10 2.12.5 3638

Super duplex

S32506 0.03 24.026.0 5.57.2 3.03.5 0.080.20 1.00 0.050.30 4042

S32520 1.4507 0.03 24.026.0 5.58.0 3.04.0 0.200.35 1.50 0.502.00 4043

255 S32550 1.4507 0.04 24.027.0 4.46.5 2.93.9 0.100.25 1.50 1.502.50 3841

2507 S32750 1.4410 0.03 24.026.0 6.08.0 3.05.0 0.240.32 1.20 0.50 4043


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Table 1 (continued): Chemical composition (weight %) and PREN range of wrought and cast duplex stainless steels*(austenitic grades shown for comparison)

Grade UNS No. EN No. C Cr Ni Mo N Mn Cu W PREN

Super duplex (continued)

S32760 1.4501 0.03 24.026.0 6.08.0 3.04.0 0.200.30 1.00 0.501.00 0.51.0 4043

S32906 1.4477 0.03 28.030.0 5.87.5 1.52.6 0.300.40 0.801.50 0.80 4143

S39274 0.03 24.026.0 6.88.0 2.53.5 0.240.32 1.00 0.200.80 1.502.50 4042

S39277 0.025 24.026.0 6.58.0 3.04.0 0.230.33 0.80 1.202.00 0.81.2 4042

Hyper duplex

S32707 0.03 26.029.0 5.59.5 4.05.0 0.300.50 1.50 1.0 4950

S33207 0.03 29.033.0 6.09.0 3.05.0 0.400.60 1.50 1.0 5253

Wrought austenitic stainless steels

304L S30403 1.4307 0.03 17.519.5 8.012.0 0.10 2.00 1819

316L S31603 1.4404 0.03 16.018.0 10.014.0 2.03.0 0.10 2.00 2425

Cast duplex stainless steels

CD4MCuGrade 1A

J93370 0.04 24.526.5 4.756.0 1.752.25 1.00 2.753.25 3233

CD4MCuN

Grade 1B

J93372 0.04 24.526.5 4.76.0 1.72.3 0.100.25 1.00 2.703.30 3436

CD3MCuN

Grade 1C

J93373 0.03 24.026.7 5.66.7 2.93.8 0.220.33 1.20 1.401.90 4042

CE8MNGrade 2A

J93345 0.08 22.525.5 8.011.0 3.04.5 0.100.30 1.00 3840

CD6MN

Grade 3A

J93371 0.06 24.027.0 4.06.0 1.752.5 0.150.25 1.00 3537

CD3MN

Cast 2205

Grade 4A

J92205 0.03 21.023.5 4.56.5 2.53.5 0.100.30 1.50 3537

CE3MN

Cast 2507

Grade 5A

J93404 1.4463 0.03 24.026.0 6.08.0 4.05.0 0.100.30 1.50 4345

CD3MWCuN

Grade 6A

J93380 0.03 24.026.0 6.58.5 3.04.0 0.200.30 1.00 0.501.00 0.51.0 4042

Cast austenitic stainless steels

CF3(cast 304L)

J92500 1.4306 0.03 17.021.0 8.012.0 1.50 1819

CF3M

(cast 316L)

J92800 1.4404 0.03 17.021.0 9.013.0 2.03.0 1.50 2425

* Maximum, unless range or minimum is indicated. Not dened in the specications.


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3.1 Chemical composition ofduplex stainless steels

It is generally accepted that the favorableproperties of duplex stainless steelscan be achieved if ferrite and austenitephases are both in the 30 to 70% range,

including in welded structures. However,duplex stainless steels are mostcommonly considered to have roughlyequal amounts of ferrite and austenite,with current commercial production justslightly favoring the austenite for besttoughness and processing characteristics.The interactions of the major alloyingelements, particularly chromium, molyb-denum, nitrogen, and nickel, are quitecomplex. To achieve a stable duplexstructure that responds well to processing

and fabrication, care must be taken toobtain the correct level of each of theseelements.

Besides the phase balance, there is asecond major concern with duplex stain-less steels and their chemical composition:the formation of detrimental intermetallicphases at elevated temperatures. Sigmaand chi phases form in high-chromium,high-molybdenum stainless steels,precipitating preferentially in the ferrite.The addition of nitrogen signicantly

delays formation of these phases.Therefore, it is critical that sufficientnitrogen be present in solid solution. Theimportance of narrow composition limitshas become apparent as experiencewith the duplex stainless steels hasincreased. The composition range thatwas originally set for 2205 (UNS S31803,Table 1) was too broad. Experience hasshown that for optimum corrosion resist-ance and to avoid intermetallic phases,the chromium, molybdenum and nitrogen

levels should be kept in the higherhalf of the ranges for S31803. Therefore,a modified 2205 with a narrowercomposition range was introduced withthe UNS number S32205 (Table 1). Thecomposition of S32205 is typical of todayscommercial production of 2205. Unless

otherwise stated in this publication, 2205refers to the S32205 composition.

3.2 The role of alloying elementsin duplex stainless steels

The following is a brief review of the effectof the most important alloying elementson the mechanical, physical and corrosionproperties of duplex stainless steels.

Chromium: A minimum of about 10.5%

chromium is necessary to form a stablechromium passive lm that is sufficient toprotect a steel against mild atmosphericcorrosion. The corrosion resistance of astainless steel increases with increasingchromium content. Chromium is a ferriteformer, meaning that the addition ofchromium promotes the body-centeredcubic structure of iron. At higher chromiumcontents, more nickel is necessary toform an austenitic or duplex (austenitic-ferritic) structure. Higher chromium alsopromotes the formation of intermetallic

phases. There is usually at least 16% Crin austenitic stainless steels and at least20% Cr in duplex grades. Chromium alsoincreases the oxidation resistance atelevated temperatures. This chromiumeffect is important because of its inuenceon the formation and removal of oxidescale or heat tint resulting from heattreatment or welding. Duplex stainlesssteels are more difficult to pickle andheat tint removal is more difficult than withaustenitic stainless steels.

Molybdenum: Molybdenum enhances thepitting corrosion resistance of stainlesssteel. When the chromium content of astainless steel is at least 18%, additions ofmolybdenum become about three timesas effective as chromium additions inimproving pitting and crevice corrosion

resistance in chloride-containingenvironments. Molybdenum is a ferriteformer and also increases the tendencyof a stainless steel to form detrimentalintermetallic phases. Therefore, it isusually restricted to less than about 7%in austenitic stainless steels and 4% induplex stainless steels.

Nitrogen: Nitrogen increases the pittingand crevice corrosion resistance ofaustenitic and duplex stainless steels. Italso substantially increases their strengthand, in fact, it is the most effective solidsolution strengthening element. It isa low cost alloying element and a strongaustenite former, able to replace someof the nickel content for austenitestabilization.The improved toughnessof nitrogen-bearing duplex stainlesssteels is due to their greater austenitecontent and reduced intermetalliccontent. Nitrogen does not prevent theprecipitation of intermetallic phases butdelays the formation of intermetallics

enough to permit processing andfabrication of the duplex grades. Nitrogenis added to highly corrosion resistantaustenitic and duplex stainless steels thatcontain high chromium and molybdenumcontents to offset their tendency to formsigma phase.

Nitrogen increases the strength of theaustenite phase by solid solutionstrengthening and also increases itswork hardening rate. In duplex stainless

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3 Chemical composition and role of

alloying elements


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Figure 1: By adding nickel, the crystallographic structure changes from body-centered cubic (little or no nickel) to face-centered cubic (at least 6% nickel 300 series). The duplex stainless steels, with their intermediate nickel content, have a microstructure in which some grains are ferritic and some areaustenitic, ideally, about equal amounts of each (Figure 2).

Figure 2: Increasing the nickel content changes the microstructure of a stainless steel from ferritic (left) to duplex (middle) to austenitic (right)(These pictures, courtesy of Outokumpu, show polished and etched samples, enlarged under a light microscope. In the duplex structure, the ferrite hasbeen stained so that it appears as the darker phase.)

steels, nitrogen is typically added and theamount of nickel is adjusted to achievethe desired phase balance. The ferrite

formers, chromium and molybdenum, arebalanced by the austenite formers, nickeland nitrogen, to develop the duplexstructure.

Nickel: Nickel is an austenite stabilizer,which promotes a change of the crystalstructure of stainless steel from body-centered cubic (ferritic) to face-centered

cubic (austenitic). Ferritic stainless steelscontain little or no nickel, duplex stain-less steels contain low to intermediate

amount of nickel from 1.5 to 7%, and the300-series austenitic stainless steels,contain at least 6% nickel (see Figures1, 2). The addition of nickel delays theformation of detrimental intermetallicphases in austenitic stainless steels butis far less effective than nitrogen in delay-ing their formation in duplex stainlesssteels. The face-centered cubic structure

is responsible for the excellent toughnessof the austenitic stainless steels. Its pres-ence in about half of the microstructure

of duplex grades greatly increases theirtoughness compared to ferritic stainlesssteels.

Ferritic (body-centered cubic) structure Austenitic (face-centered cubic) structure

add nickel

Ferritic structure

add nickel

Duplex structure Austen itic stru cture

add nickel


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4 Metallurgy of duplex stainless steels

4.1 Austenite-ferrite phase balance

The iron-chromium-nickel ternary phasediagram is a roadmap of the metallurgicalbehavior of the duplex stainless steels.A section through the ternary diagram at68% iron (Figure 3) illustrates that thesealloys solidify as ferrite (), which thenpartially transforms to austenite () asthe temperature falls, depending on alloy

composition. When water quenching fromthe solution annealing temperature, amicrostructure of roughly 50% austeniteand 50% ferrite can be achieved at roomtemperature. Increasing the nitrogencontent increases the ferrite to austenitetransformation start temperature (Ref. 1)and improves the structural stability ofthe grade particularly in the HAZ.

The relative amounts of ferrite andaustenite that are present in a mill product

or fabrication of a given duplex grade

depend on the chemical compositionand thermal history of the steel. Minorchanges in composition can have asignicant effect on the relative volumefraction of these two phases, as thephase diagram indicates. Individualalloying elements tend to promote eitherthe formation of austenite or ferrite.The ferrite/austenite phase balance in themicrostructure can be predicted with

multivariable linear regression as follows:

C& = C + 1.73 S + 0.88 M

N& = N + 24.55 C + 21.75 N + 0.4 C

% F&& = -20.93 + 4.01 C& 5.6 N&

+ 0.016 T

where T (in C) is the annealing tempera-ture ranging from 10501150C and theelemental compositions are in weight%

(Ref. 2).

The goal of obtaining the desired phasebalance of close to 45 to 50 % ferritewith the remainder austenite, is achievedprimarily by adjusting chromium, molyb-denum, nickel and nitrogen contents, andthen by controlling the thermal history.

For mill products, solution annealing atan appropriate solution annealingtemperature followed by immediate water

quenching gives the best results. It isimportant to keep the time between exitingthe furnace and water quenching asshort as possible. This is to minimize heatloss of the product which could lead todetrimental phase precipitation beforewater quenching to room temperature.

For welded structures, the heat input hasto be optimized for each grade and weldconguration so that the cooling ratewill be quick enough to avoid detrimental

phases but not so fast that there remainsexcessive ferrite in the vicinity of thefusion line. In practice this situation mayoccur when welding widely differingsection sizes or when welding heavysections with very low heat inputs duringfabrication. In these cases the thickmetal section can quench the thin weldso rapidly that there is insufficient time forenough of the ferrite to transform toaustenite, leading to excessive amountsof ferrite, particularly in the HAZ.

Because nitrogen increases the tempera-ture at which the austenite begins toform from the ferrite, as illustrated inFigure 3, it also increases the rate of theferrite to austenite transformation.Therefore, even at relatively rapid coolingrates, the equilibrium level of austenitecan nearly be reached if the gradehas sufficient nitrogen. In the second-generation duplex stainless steels, thiseffect reduces the potential of excessferrite in the HAZ.

FCL

L+

L++ L+

+

[N]

1400

800

0

30 25 20 15

%Ni

%Cr5 10 15

1200

1000

2192

2552

1832

1472

Figure 3: Section through the Fe-Cr-Ni ternary phase diagram at 68% iron (small changes in thenickel and chromium content have a large influence on the amount of austenite and ferrite in duplexstainless steels.)


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F

A

Figure 5: Microstructure of a 2205 sample agedat 850C (1560F) for 40 minutes showing sigmaphase precipitation (arrows) on the austenite/

ferrite grain boundaries. The ferrite (F) phaseappears darker than the austenite (A) phase in themicrograph (Ref. 3).

1100

1000

900

800

700

600

500

400

300

200

0

Time (minutes)

TemperatureC

1 10 100 1000 10000

2012

1832

1652

1472

1292

1112

932

752

572

392

alpha

prime Toughness

Sigma phase

Nitride

Figure 4: Isothermal precipitation diagram for 2205 duplex stainless steel, annealed at 1050C

(1920F). (The sigma phase and nitride precipitation curves for 2507 and 2304, respectively, are shownfor comparison)

Figure 6: Cooling from the solution annealing temperature should be fast enough (cooling curve A)to avoid the sigma phase field (cooling curve B).

TemperatureF

Hardness

4.2 Precipitates

Detrimental phases can form in a matter

of minutes at the critical temperature,as can be seen in the isothermal precipi-tation diagram for 2507 and 2205 duplexstainless steels in Figure 4 (Ref. 4, 5, 6,7). They can reduce corrosion resistanceand toughness signicantly. Therefore,the cumulative time in the temperaturerange where they can form, especiallyduring welding and cooling afterannealing, has to be minimized. Modernduplex grades have been developed tomaximize corrosion resistance and retard

precipitation of these phases, allowingsuccessful fabrication. However, onceformed, they can only be removed by fullsolution annealing and subsequentwater quenching.

Sigma phase (Figure 5) and other inter-metallic phases such as chi can precipitatefrom the ferrite at temperatures belowaustenite formation on cooling too slowlythrough the temperature range of 7001000C (13001830F). Sigma phaseformation in mill products can, therefore,be avoided by water quenching the steelas rapidly as possible from the solutionannealing temperature and avoiding thesigma phase eld (Figure 6).

A

B

600

Temperature(C)

Time

700

800

900

1000

1100

Sigma phase

2507

2304

2205


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The driving force for sigma phaseformation increases with increasingmolybdenum and chromium content. Themore highly alloyed grades, from 2205on up are therefore most affected.Precipitates tend to form quicker withincreasing alloy content as shown inFigure 4 where the start curve for 2507 isto the left (shorter time) of the one for2205. Lean duplex grades such as 2304do not readily form intermetallic phases

and nitride precipitation is more likelyas shown in Figure 4.

The presence of sigma phase decreasesthe pitting resistance of duplex stainlesssteels, due to the depletion of chromiumand molybdenum in surrounding areas.This depletion leads to a local reductionof the corrosion resistance next to theprecipitates. Toughness and ductility arealso sharply reduced when intermetallicphase precipitation occurs.

Chromium nitride precipitation can forsome grades start in only 12 minutes atthe critical temperature. It can occur in thegrain or phase boundaries as a result oftoo slow cooling through the temperaturerange of 600900C (11001650F).Nitride formation is not very common inmost duplex grades, but it can be an issuewith some lean duplex stainless steels,due to relatively high nitrogen contentand reduced nitrogen solubility compared

to higher alloyed grades. Similar to sigmaphase, it can largely be avoided in thesteel mill by water quenching from anadequate solution annealing temperature.

Chromium nitride can, however, alsoprecipitate in the HAZ and weld metal inwelded fabrications. A high ferrite contentin the vicinity of the fusion line, due tovery rapid cooling in this area, can lead tonitrogen oversaturation. Ferrite in generalhas very low solubility for nitrogen which

decreases further as the temperaturedecreases. So if nitrogen is caught in theferrite phase it might precipitate as

chromium nitride upon cooling. A slowercooling rate will result in a competitionbetween nitride precipitation and anincrease of austenite re-transformation.More austenite allows more nitrogen todissolve in the austenite grains, reducingthe nitrogen oversaturation of the ferriticgrains and the amount of chromiumnitride. The precipitation of chromiumnitrides in welds can therefore be de-creased by increasing the austenite levelthrough higher heat input (slower cooling)

or through additions of austenite-promoting elements such as nickel in theweld metal or nitrogen in the shieldinggas.

If formed in large volume, chromiumnitrides may adversely affect corrosionresistance and toughness properties.

Alpha prime can form in the ferrite phaseof duplex stainless steels below about525C (950F). It takes significantlylonger to form than the other phasesdiscussed above and is first noticed asan increase in hardness and only lateras a loss in toughness (Figure 4).

In ferritic stainless steels alpha primecauses the loss of ambient temperaturetoughness after extended exposure totemperatures around 475C (885F);this behavior is known as 475C/885Fembrittlement. Fortunately, becauseduplex stainless steels contain 50%austenite, this hardening and embrittling

effect is not nearly as detrimental as itis in fully ferritic steels. It does affect allduplex stainless steel grades, but ismost pronounced in the molybdenum-containing grades and much less in thelean duplex grades.

Alpha prime embrittlement is rarely aconcern during fabrication because of thelong times required for embrittlementto occur. One exception, which has to becarefully evaluated, is stress relief

Duplex stainless steel has to be water quenched immediately after solution annealing. Bosch-Gotthard-Htte


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13

Grade Condition ASME TV

C F C F

2304 Unwelded 315 600 300 570

2304 Welded, matching filler 315 600 300 570

2304 Welded with 2205/2209 315 600 250 480

2205 Unwelded 315 600 280 535

2205 Welded 315 600 250 480

2507 Seamless tubes 315 600 250 480

Alloy 255 Welded or unwelded 315 600

Table 2: Upper temperature limits for duplex stainless steel for maximum allowable stress values in pressure vessel design codes

Table 3: Typical temperatures for precipitation reactions and other characteristic reactions in duplex stainless steels

2205 2507

C F C F

Solidification range 14701380 26802515 14501350 26402460

Scaling temperature in air 1000 1830 1000 1830

Sigma phase formation 700950 13001740 7001000 13001830

Nitride, carbide precipitation 450800 8401470 450800 8401470

475C/885F embrittlement 300525 575980 300525 575980

treatment of duplex-clad carbon steelconstructions. Any heat treatment in thecritical temperature range for alpha prime

formation of 300525C (575980F)(or for intermetallic phase formation of700950C (13002515F), for 2205)has to be avoided. If a stress relief treat-ment is required, it is best to consult theclad plate producer for advice.

However, the upper temperature limit forduplex stainless steel service is controlled

by alpha prime formation. Pressure vesseldesign codes have therefore establishedupper temperature limits for the maximum

allowable design stresses. The GermanTV code distinguishes between weldedand unwelded constructions and is moreconservative in its upper temperaturelimits than the ASME Boiler and PressureVessel Code. The temperature limits forthese pressure vessel design codesfor various duplex stainless steels aresummarized in Table 2.

The second generation duplex stainlesssteels are produced with very lowcarbon content so that carbide formation

to a detrimental extent is typically nota concern.

Table 3 summarizes a number ofimportant precipitation reactions andtemperature limitations for duplexstainless steels.


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5 Corrosion resistance

Duplex stainless steels exhibit a highlevel of corrosion resistance in mostenvironments where the standardaustenitic grades are used. However,there are some notable exceptions wherethey are decidedly superior. This resultsfrom their high chromium content, whichis benecial in oxidizing acids, alongwith sufficient molybdenum and nickel toprovide resistance in mildly reducing

acid environments. The relatively highchromium, molybdenum and nitrogenalso give them very good resistance tochloride-induced pitting and crevicecorrosion. The duplex structure is anadvantage in potential chloride stresscorrosion cracking environments. If themicrostructure contains at least thirty

percent ferrite, duplex stainless steels arefar more resistant to chloride stresscorrosion cracking than austenitic stainlesssteel Types 304 or 316. Ferrite is, however,susceptible to hydrogen embrittlement.Thus, the duplex stainless steels do nothave high resistance in environmentsor applications where hydrogen may becharged into the metal and causehydrogen embrittlement.

5.1 Resistance to acids

To illustrate the corrosion resistance ofduplex stainless steels in strong acids,Figure 7 provides corrosion data forsulfuric acid solutions. This environmentranges from mildly reducing at low acid

concentrations, to oxidizing at highconcentrations, with a strongly reducingmiddle composition range in warm andhot solutions. Both 2205 and 2507duplex stainless steels outperform manyhigh nickel austenitic stainless steels insolutions containing up to about 15%acid. They are better than Types 316 or317 through at least 40% acid. Theduplex grades can also be very useful in

oxidizing acids of this kind containingchlorides. The duplex stainless steels donot have sufficient nickel to resist thestrong reducing conditions of mid-concentration sulfuric acid solutions, orhydrochloric acid. At wet/dry intefaces inreducing environments where there isconcentration of the acid, corrosion,

160

Boiling point curve

Type 316

317 LMN

2205 2507

904L

254 SMO

Alloy 20

T

emperature(C) Te

mperature(

F)

140

120

100

80

60

40

20

0

320

284

248

212

175

140

104

68

32

0

Sulfuric acid concentration (weight %)

20 40 60 80 100

Figure 7: Corrosion in non-aerated sulfuric acid, 0.1 mm/yr (0.004 inch/yr) isocorrosion diagram (laboratory tests usingreagent grade sulfuric acid). Source: Producer data sheets, 254 SMO is a trademark of Outokumpu

14


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2205 continuous sulphate pulp digester and impregnation tower,Sodra Cell Mnsteras, Sweden. Kvaerner Pulping

especially of the ferrite, may be activatedand proceed rapidly. Their resistanceto oxidizing conditions makes duplex

stainless steels good candidates for nitricacid service and the strong organic acids.This is illustrated in Figure 8 for solutionscontaining 50% acetic acid and varyingamounts of formic acid at their boilingtemperatures. Although Types 304 and316 will handle these strong organicacids at ambient and moderate tempera-tures, 2205 and other duplex gradesare superior in many processes involvingorganic acids at high temperature. Theduplex stainless steels are also used in

processes involving halogenated hydro-carbons because of their resistance topitting and stress corrosion.

5.2 Resistance to caustics

The high chromium content and presenceof ferrite provides for good performanceof duplex stainless steels in causticenvironments. At moderate temperatures,corrosion rates are lower than those ofthe standard austenitic grades.

5.3 Pitting and crevicecorrosion resistance

To discuss pitting and crevice corrosionresistance of stainless steels, it is usefulto introduce the concept of criticaltemperatures for pitting corrosion. For aparticular chloride environment, eachstainless steel can be characterized bya temperature above which pittingcorrosion will initiate and propagate to a

visibly detectable extent within about24 hours. Below this temperature, pittinginitiation will not occur. This temperatureis known as the critical pitting temperature(CPT). It is a characteristic of the particularstainless steel grade and the specicenvironment. Because pitting initiation isstatistically random, and because of thesensitivity of the CPT to minor within-gradevariations or within product variations,the CPT is typically expressed for variousgrades as a range of temperatures.

0.3

Type 316L Type 317L

Alloy 28

2205

254 SMO

2507 no attack

0.25

0.2

0.15

0.1

0.05

0

12

10

8

6

4

2

0

0 5 10 15 20 25

Corrosionrate(mm/y)

Corrosionrate(mils/y)

Formic acid concentration (weight %)

Figure 8: Corrosion of duplex and austenitic stainless steels in boiling mixtures of 50% acetic acid andvarying proportions of formic acid. Source: Sandvik

15


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16

The high chromium, molybdenum andnitrogen contents in duplex gradesprovide very good resistance to chloride-induced localized corrosion in aqueousenvironments. Depending on the alloycontent, some duplex grades are amongthe best performing stainless steels.Because they contain relatively highchromium content, duplex stainless steelsprovide a high level of corrosion resistancevery economically. A comparison of

pitting and crevice corrosion resistancefor a number of stainless steels in thesolution annealed condition as measuredby the ASTM G 482 procedures (6%ferric chloride) is given in Figure 9.Critical temperatures for materials in theas-welded condition would be expectedto be somewhat lower. Higher criticalpitting or crevice corrosion temperaturesindicate greater resistance to the initiation

of these forms of corrosion. The CPTand CCT of 2205 are well above those ofType 316. This makes 2205 a versatilematerial in applications where chloridesare concentrated by evaporation, asin the vapor spaces of heat exchangersor beneath insulation. The CPT of 2205indicates that it can handle many brackishwaters and deaerated brines. It hasbeen successfully used in deaeratedseawater applications where the surface

has been maintained free of depositsthrough high ow rates or other means.2205 does not have enough crevicecorrosion resistance to withstandseawater in critical applications such asthin wall heat exchanger tubes, or wheredeposits or crevices exist. However,the more highly alloyed duplex stainlesssteels with higher CCT than 2205, forexample, the super duplex and hyper

However, with the research tool describedin ASTM G 1501, it is possible todetermine the CPT accurately and reliablyby electrochemical measurements.

There is a similar temperature for crevicecorrosion, which occurs in gasket joints,under deposits and in bolted joints wherea crevice is formed in fabricated products.The critical crevice temperature (CCT) isdependent on the individual sample of

stainless steel, the chloride environment,and the nature (tightness, length, etc.) ofthe crevice. Because of the dependenceon the geometry of the crevice andthe difficulty of achieving reproduciblecrevices in practice, there is more scatterfor the measurement of CCT than forthe CPT. Typically, the CCT will be 15 to20C (27 to 36F) lower than the CPTfor the same steel and same corrosionenvironment.

90

100

CCT (C) CPT (C)

80

70

60

50

40

30

20

10

0

-10

-20

Temperature(C)

S32101304L 316L 6Mo 2304 2205S82441 255 2507 S32707

Figure 9: Critical pitting and crevice corrosion temperatures for unwelded austenitic stainless stee ls (left side) and duplex stainless steels (right side)in the solution annealed condition (evaluated in 6% ferric chloride by ASTM G 48).

1 ASTM G 150 Standard test method for electrochemical critical pitting temperature testing of stainless steels2 ASTM G 48 Standard test method for pitting and crevice corrosion resistance of stainless steels and related alloys by ferric chloride solution


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17

100

90

80

70

60

50

40

30

20

10

0

Pct.

Y.S.

forSCC

316 S32101 2205 2507 904L 6Mo

Figure 10: Stress corrosion cracking resistance of mill annealed austenitic and duplex stainless steels inthe drop evaporation test with sodium chloride solutions at 120C (248F) (stress that caused crackingshown as a percentage of yield strength). Source: Outokumpu

duplex grades, have been used in manycritical seawater handling situationswhere both strength and chloride resist-

ance are needed. Although the superduplex grades do not corrode in lowertemperature seawater, they have limits inhigher temperature service. The improvedcorrosion resistance of hyper duplexstainless steels extends their use toaggressive chloride environments, suchas in hot tropical seawater, especiallywhen there are crevices.

Because the CPT is a function of thematerial and the particular environment,

it is possible to study the effect ofindividual elements. Using the CPT asdetermined by ASTM G 48 Practice A,statistical regression analysis was appliedto the compositions of the steels (eachelement considered as an independentvariable) and the measured CPT (thedependent variable). The result was thatonly chromium, molybdenum, tungsten,and nitrogen showed consistentmeasurable effect on the CPT accordingto the relationship:

CPT = $" + C + 3.3 (M + 0.5!)

+ 16N.

In this relationship, the sum of the fouralloy element variables multiplied bytheir regression constants is commonlycalled the Pitting Resistance EquivalentNumber (PREN). The coefficient fornitrogen varies among investigators and16, 22, and 30 are commonly used(Ref. 8). The PREN is useful for rankinggrades within a single family of steels.

However, care must be taken to avoidinappropriate over-reliance on thisrelationship. The independent variableswere not truly independent because thesteels tested were balanced compositions.The relationships are not linear, andcross relationships, such as the synergiesof chromium and molybdenum, wereignored. The relationship assumes anideally processed material, but does not

address the effect of intermetallic phases,non-metallic phases, or improper heattreatment that can adversely affect

corrosion resistance.

5.4 Stress corrosion crackingresistance

Some of the earliest uses of duplexstainless steels were based on their re-sistance to chloride SCC. Compared withaustenitic stainless steels with similarchloride pitting and crevice corrosion-resistance, the duplex stainless steelsexhibit signicantly better SCC resistance.

Many of the uses of duplex stainlesssteels in the chemical process industriesare replacements for austenitic grades inapplications with a signicant risk ofSCC. However, as with many alloys,the duplex stainless steels may be sus-ceptible to SCC under certain conditions.This may occur in high temperature,

chloride-containing environments, orwhen conditions favor hydrogen-inducedcracking. Examples of environments in

which SCC of duplex stainless steelsmay be expected include the boiling 42%magnesium chloride test, drop evapora-tion when the metal temperature is high,and exposure to pressurized aqueouschloride systems in which the temperatureis higher than what is possible at ambientpressure.

An illustration of relative chloride SCCresistance for a number of mill annealedduplex and austenitic stainless steels in

a severe chloride environment is given inFigure 10 (Ref. 9). The drop evaporationtest used to generate these data is veryaggressive because it is conducted ata high temperature of 120C (248F) andthe chloride solution is concentrated byevaporation. The three duplex steelsshown, UNS S32101, 2205 and 2507, will


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18

Cracking anticipated Cracking possible Cracking not anticipated Insufficient data

Grade Type 304LType 316L

3RE60 S32101S32202

2205 Super duplex Hyper duplex

42% MgCl2, boiling,154C, U-bend

35% MgCl2, boiling,125C, U-bend

Drop evap.,0.1M NaCl,

120C, 0.9 x Y.S.

Wick test 1500 ppm Clas NaCl 100C

33% LiCl2, boiling,120C, U-bend

40% CaCl2,100C, 0.9 x Y.S.

2528% NaCl, boiling,106C, U-bend

26% NaCl, autoclave,155C, U-bend

26% NaCl, autoclave,200C, U-bend

600 ppm Cl (NaCl),autoclave, 300C, U-bend

100 ppm Cl (sea salt + O2),autoclave, 230C, U-bend

Table 4: Comparative stress corrosion cracking resistance of unwelded duplex and austenitic stainless steels in accelerated laboratory tests.Source: various literature sources

eventually crack at some fraction of theiryield strength in this test, but that fractionis much higher than that of Type 316

stainless steel. Because of their resistanceto SCC in aqueous chloride environmentsat ambient pressure, for example, underinsulation, the duplex stainless steelsmay be considered in chloride crackingenvironments where Types 304 and316 have been known to crack. Table 4summarizes chloride SCC behavior of

different stainless steels in a variety oftest environments with a range ofseverities. The environments listed near

the top of the table are severe becauseof their acid salts, while those nearthe bottom are severe because of hightemperatures. The environments in thecenter are less severe. The standardaustenitic stainless steels, those with lessthan 4% Mo, undergo chloride SCC inall these environments, while the duplex

stainless steels are resistant throughoutthe mid-range, moderate conditionsof testing.

Resistance to hydrogen-induced SCC isa complex function, not only of ferritecontent, but also of strength, temperature,charging conditions, and the appliedstress. In spite of their susceptibility tohydrogen cracking, the strengthadvantages of duplex stainless steels


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19

Duplex stainless steel pipes. Butting

300

SCC

no SCC

Localizedcorrosion

PassiveNo attack

Active

General corrosion

20% NaCl

H2S pressure (MPa)

Temperature(C) Te

mperature(K)

200

100

0

10-2 10-1 10 101

500

400

300

G G G

G G

GG

L1

L1N

L1

L1A

C

B

Figure 11: Corrosion of 2205 duplex stainless steel in 20% sodium chloride-hydrogen sulfideenvironments based on electrochemical prediction and experimental results.

can be used in hydrogen-containingenvironments provided the operatingconditions are carefully evaluated and

controlled. The most notable of theseapplications is high strength tubularshandling mixtures of slightly sour gas andbrine. An illustration showing regimesof immunity and susceptibility for 2205 insour environments containing sodiumchloride is shown in Figure 11 (Ref. 10).


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20

6 End user specifications and quality

control

A critical practical issue in specicationand quality control of duplex stainlesssteel fabrications is the retention ofproperties after welding. It is essentialfor the duplex stainless steel startingmaterial to have the composition andprocessing that leads to good properties

after welding by a qualied procedure.

6.1 Standard testingrequirements

6.1.1 Chemical composition

The ASTM or EN specifications are theappropriate starting point for selecting asecond-generation duplex stainless steel.Nitrogen is benecial, both with respectto avoiding excessive ferrite in the HAZ

and with respect to greater metallurgicalstability. The upper limit of nitrogen in aduplex stainless steel is the solubility ofnitrogen in the melt, and that is reectedin the maximum of the specied nitrogenrange in the standard specications.However, the minimum nitrogen listedmay or may not reect the level neededto provide the best welding response.An example of this is S31803, the originalspecication for 2205 (Ref. 11).

At the lower end of the 0.080.20% N

range permitted in S31803, 2205 hadinconsistent response to heat treatingand welding. Practical experience led tothe recognition that 0.14% minimumnitrogen is necessary for 2205 weldedfabrications. Because this requirementwas frequently specied, the S32205version of 2205 was introduced intothe specication for the convenience ofthe end users requiring welding. The

super duplex stainless steels also havehigher nitrogen ranges, reecting therecognition of the importance of nitrogen.

There have been some end user duplexstainless steel specications basedon the PREN relationship. While a PREN

value may be effective at ranking thecorrosion resistance of various gradeswithin a family of correctly balancedcompositions, a composition modiedto meet a specic PREN does notnecessarily lead to correct metallurgicalbalance. The PREN may assist inselecting one of the listed grades, butwhen applied to variations within agrade, it suggests that chromium andmolybdenum are substitutable withnitrogen. But metallurgically, chromiumand molybdenum promote ferrite andintermetallic phases, while nitrogenpromotes austenite and inhibits formationof intermetallic phases.

Therefore, the selection of compositionfor duplex grades is best based on thestandard grades listed in the specication,possibly with restriction of nitrogen tothe upper end of the specication rangefor each grade. Whatever composition isspecied, it should be the same materialthat is used in qualication of welding

procedures, so that the qualications aremeaningful in terms of the results thatmay be expected in the fabrication.

6.1.2 Solution annealing and quenching

In addition to chemical composition,the actual annealed condition of millproducts is also important for a consistentresponse to welding. In an austenitic

stainless steel, the purpose of annealingis to recrystallize the metal and todissolve any carbides. With the low carbonL-grades, the stainless steel may bewater quenched or air cooled relativelyslowly because the time to re-formdetrimental amounts of carbides is quite

long. However, with the duplex stainlesssteels, even with the ideal nitrogencontent, exposures of a few minutes inthe critical temperature range aredetrimental to corrosion resistance andtoughness (Ref. 12). When a mill productis slowly cooled in the steel mill, thetime that it takes the material to passthrough the 700980C (13001800F)range is no longer available for furtherthermal exposures in that temperaturerange, for example, when welding. So thewelder will have less time to make aweld that is free of intermetallic phasesin the HAZ.

While specications such as ASTMpermit some duplex grades to be waterquenched or rapidly cooled by othermeans, the best metallurgical conditionfor welding is achieved by the mostrapid quenching from the annealingtemperature. However, this ignores thedistortion and increased residual stressesinduced by water quenching. In the case

of sheet product, air cooling is highlyeffective in modern coil processing lines;but for plate and thicker section products,water quenching produces the bestmetallurgical condition for welding.Allowing a plate or a tting to cool into the700980C (13001800F) range priorto quenching may lead to the formation ofintermetallic phases.


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21

Another approach to assure an optimalstarting condition is to require thatmill products be tested for the absence

of detrimental intermetallic phases.ASTM A 9233 and ASTM A 10844 usemetallographic examination, impacttesting, or corrosion testing to demonstratethe absence of a harmful level of detri-mental phases. This test considers onlywhether harmful precipitation hasalready occurred and not the amount ordegree of detr imental precipitation. Withthis type of testing the mill procedure isveried to ensure that harmful phases havenot been formed during mill processing.

This testing is analogous to ASTM A 262 5or EN ISO 3651-26 testing of austeniticstainless steels for sensitization dueto chromium carbide precipitation.ASTM A 923 covers 2205, 2507, 255 andS32520, and ASTM A 1084 covers thelean duplex grades S32101 and S32304.Many fabricators have adopted theseand similar tests or other acceptancecriteria, as a part of their qualication forwelding procedures of fabricatedproducts.

6.2 Special testing requirements

6.2.1 Tensile and hardness tests

The duplex stainless steels have highstrength relative to the austeniticstainless steels. However, there havebeen occasional end user specicationsin which a maximum has been imposedon either the strength or hardness.Imposing maximums on strength orhardness is probably a carryover from

experience with martensitic stainlesssteels where high strength or hardnessis caused by untempered martensite.

However, the duplex stainless steels willnot form martensite during cooling.High strength and hardness in a duplexstainless steel are the result of highnitrogen content, the duplex structureitself, and work hardening that may occurin forming or straightening operations.

Hardness testing can be an effectivemeans of demonstrating that there hasnot been excessive cold working in

fabrication; but it is important that whenthe hardness test is being used for thispurpose, the measurement is made at alocation midway between the surfaceand center of the section and not on asurface that may have been locally andsupercially hardened.

3 ASTM A 923 Standard test methods for detecting detrimental intermetallic phases in duplex austenitic/ferritic stainless steels4 ASTM A 1084 Standard test method for detecting detrimental phases in lean duplex austenitic/ferritic stainless steels5 ASTM A 262 Standard practices for detecting susceptibility to intergranular attack in austenitic stainless steels6 EN ISO 3651-2 Determination of resistance to intergranular corrosion of stainless steels Part 2: Ferritic, austenitic and ferritic-austenitic

(duplex) stainless steels corrosion test in media containing sulfuric acid

Inside a 2205 tank on a marine chemical tanker. Outokumpu


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22

6.2.2 Bend tests

Bend tests may demonstrate that mill

products are free of cracking from rolling,but may be difficult for heavy sections,small pieces, or certain geometries.Bend tests are not a conservativeindication of quality in duplex stainlesssteel because the point of bendingmay not coincide with the location of anunacceptable condition. Some conditionssuch as centerline intermetallic phaseare unlikely to be detected because ofthe directionality of bending.

Bend tests are commonly used as part ofthe qualication of welding proceduresfor the austenitic stainless steels becausethere is a risk of hot cracking of theweld, especially for highly austenitic weldstructures that are heavily constrained.The usefulness of bend tests for detectingproblems of weld integrity is greatlyreduced in duplex stainless steel becausethey have no tendency for hot cracking.Bend tests might detect grossly excessiveferrite if the test location coincidesprecisely with the affected region, but bendtests are unlikely to detect the occurrenceof intermetallic phases at the low levelsknown to be harmful to corrosion resistanceand toughness.

6.2.3 Impact testing and metallographicexamination for detrimental phases

There are two ways that an impact testcan be used to specify material or qualifya procedure:

Test at conditions known to detectunacceptable material, for example,excessive ferrite or the presence ofdetrimental phases;

Demonstrate that a fabrication hasproperties sufficient for the intendedservice.

For the rst way to use impact testing,ASTM A 923 provides acceptance criteriafor duplex and super duplex stainlesssteels and ASTM A 1084 for lean duplexstainless steels. For example, the lossof toughness described in ASTM A 923,Method B, in a standard longitudinalCharpy test at -40C/F to less than 54J(40 ft-lb) is indicative of an unacceptablecondition in a mill annealed product.To assure that the heat treatment andquenching are satisfactory, ASTM A 923Method B (or Method C, the corrosiontest) should be required for eachheat lot of mill product as a productioncontrol measure. However, ASTM A 923also allows the use of metallographic

examination (Method A), as a screeningtest for acceptance but not rejection.Because of the high level of metallo-

graphic skill required to implement MethodA, it may be prudent for the end userto require the Method B Charpy impacttest in addition to the metallographicexamination.

One advantage of ASTM A 923 MethodA is the identication of centerlineintermetallic phase, as shown in Figure 7of ASTM A 923. Centerline intermetallicphase will disqualify a material withrespect to screening by Method A, but

may not necessarily result in rejection ofthe material in ASTM A 923 Method B,impact testing. Because this centerlineintermetallic phase may lead to delamina-tion of the plate during forming, thermalcutting, or welding, the user should requirethat Method A be performed in additionto Method B or C, and that any materialshowing centerline intermetallic phaseshould be rejected. Although ASTM A 923states that Method A may not be usedfor rejection, an end user is permitted toimpose more stringent requirements.Material that shows centerline intermetallicphase near mid-thickness as indicated byASTM A 923 Figure 7 should be rejected.

The second way to use impact testing,evaluating base metal, fusion zone andHAZ at lower temperatures than theintended service, may be cost effectiveand conservative. For weld evaluation,the test temperature and acceptancecriterion must be specic to the type ofweld and meaningfully related to the

service conditions. The toughness will notbe as high as that of a solution annealedduplex stainless steel mill product.Lower toughness in weld metal is notnecessarily indicative of intermetallicphases but is more frequently a result ofincreased oxygen content, especiallyfor the ux-shielded welding procedures.

2507 stainless steel falling film evaporator. Gary Carinci, TMR Stainless


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23

ASME issued new requirements applicableto duplex stainless steels with sectionthickness greater than 9.5 mm (0.375 inch)(Ref. 13). These requirements use Charpyimpact tests at or below the minimumdesign metal temperature (MDMT), withacceptance criteria expressed in lateralexpansion, to demonstrate that the starting

material and production welds are toughenough for the intended service. TheASME test differs from the ASTM A 923test in that the ASME test requires that theCharpy test consists of three specimensand requires reporting both minimum andaverage results. ASME requires testingof base metal, weld metal and HAZ(nine samples total) for each heat of basematerial and each lot of ller.

For economy of testing with conservativeresults, it is possible to use the lower ofthe two testing temperatures (-40C/F inASTM A 923 or MDMT in the ASME Code),and measure the toughness by bothimpact energy and lateral expansion fortriplicate specimens.

6.2.4 Phase balance as determinedby metallography or magneticmeasurements

The austenite-ferrite phase balance ofduplex stainless steel mill productsexhibits very little heat-to-heat or lot-to-lotvariation because they are produced tovery narrow chemical composition rangesand well-dened annealing practices.Typically, 2205 contains 4050% ferrite.

For this reason, the determination of thephase balance in annealed mill productsis of limited value.

However, a ferrite determination maybe appropriate for qualication of weldingprocedures to guard against excessiveferrite in the HAZ. An accurate deter-

mination of phase balance for a duplexstainless steel usually requires ametallographic examination and pointcount, for example ASTM E 5627 (manual)or ASTM E 12458 (automated). Becauseduplex stainless steels are ferromagneticwith an exceedingly ne spacing ofaustenite and ferrite, use of magneticdetection methods has limited reliabilitywithout reference standards of identicalgeometry and metallographically

Installation of duplex stainless steel rebar on a large bridge deck. Hardesty & Hanover, LLP

7 ASTM E 562 Standard test method for determining volume fraction by systematic manual point count8 ASTM E 1245 Standard practice for determining the inclusion or second-phase constituent content of metals by automatic image analysis


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Grade Location Test Testing temperatureC ( F)

S32101 Base metal ASTM A 1084C 25 (77)



S31803 Weld metal ASTM A 923C 22 (72)


S32205 Weld metal ASTM A 923C 22 (72)




Table 5: Corrosion test temperature for different duplex grades according to ASTM A 1084Cand ASTM A 923C. The maximum acceptable corrosion rate is 10 mg/dm2 day.

measured phase balance. AWS A4.29

and EN ISO 824910 describe proceduresfor calibrating magnetic instruments

to measure ferrite in duplex stainless steelwelds and reporting the results in FerriteNumber, FN. The range of phase balanceacceptable for a weld is substantiallywider than that for the base metal. Iftoughness and corrosion resistance of theweld and HAZ are acceptable, asdemonstrated by tests such as those ofASTM A 923, then a range of 2575%ferrite can provide the desired propertiesof the duplex stainless steel. Magneticmeasurements in the range of FN 3090

are considered acceptable.

Requiring determination of phase balancefor material that is already in service centeror stockist inventory is more expensivethan imposing the same requirement onmaterial as it is being produced at a mill.Obtaining the sample and performinga separate test may also reduce timelyavailability.

Because intermetallic phases are non-magnetic, magnetic testing cannot be usedto directly detect sigma and chi phases.However, low-magnetic ferrite readings

on a duplex stainless steel may be anindication that the ferrite has been trans-formed to an intermetallic phase. Duplexstainless steels exposed to the inter-metallic precipitation temperature range

for an extended period of time duringheat treating or cooling may exhibit lowferrite contents.

6.2.5 Corrosion testing

Corrosion testing of solution annealedmill products, in accordance withASTM A 923/A 1084 Method C, is one ofthe most cost-effective testing methodsfor detection of detrimental conditions.The presence of intermetallic phases,and chromium nitride, in an excessivelyferritic phase balance, are detected asa loss of pitting resistance. These phases

cause losses of 15C, or more, fromthe CPT typically expected for the properlyannealed material. Measurement of theactual critical pitting temperature for aspecimen is relatively expensive becauseit requires multiple tests per ASTM G 48 orASTM G 150 testing of a single specimen.However, performing a single corrosion

Installation of hyper duplex stainless steel bolts to preserve the historic wooden Vasa ship in Sweden. Anneli Karlsson, the Swedish National Maritime Museums

9 AWS A4.2 Standard procedure for calibrating magnetic instruments to measure delta ferrite content of austenitic and duplex ferritic-austeniticstainless steel weld metal

10 EN ISO 8249 Welding Determination of ferrite number (FN) in austenitic and duplex ferritic-austenitic Cr-Ni stainless steel weld metals

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test (ASTM A 923 Method C) 10 to 15Cbelow the typical CPT for a duplexstainless steel will reveal the presence

of detrimental phases. When using acorrosion test to detect the presence ofharmful phases, any pitting on the facesor on the edges should be included asa basis for rejection. While the edge maynot be exposed in actual service, thistest is intended to detect intermetallicphases, and these are more likely to bepresent at the centerline, which isevaluated when edge attack is included.

Prior to the development of ASTM A 923,

the corrosion test was generallycalled out by referencing the modiedASTM G 48 test. However, G 48 is adescription of a laboratory research pro-cedure, rather than a material acceptancetest. A requirement for testing by G 48is not complete without a determination ofwhich G 48 Practice is to be performed,and a statement of other testing variablesincluding:

Surface preparation, Test temperature, Test duration, Inclusion or exclusion of edge corrosion, Denition of an acceptance criterion.

ASTM A 923 is an acceptance testdesigned to demonstrate the absence ofdetrimental intermetallic phases in millproducts in a cost effective and relativelyrapid way. ASTM A 923, Method C,expresses the acceptance criterion as acorrosion rate. That may seem surprisingwhen the issue is the detection of pitting

corrosion; however, this approach wasused for two reasons:

1. By basing the acceptance on weightloss, the burdensome and potentiallysubjective issue of what is a pit on themetal surface is eliminated. The weightloss required for rejection is largeenough to be readily measured, butsmall enough to easily detect the kindof pitting associated with the presenceof intermetallic phases in a 24-hour

test.

2. By using a corrosion rate, almost anyspecimen size or shape can be testedprovided that the total surface areacan be determined.

The corrosion test is conservative andnot sensitive to specimen geometry andlocation, in contrast to a Charpy test,which is sensitive to orientation and notchlocation. The corrosion test is appropriateas part of the qualification of weld

procedures, and as a cost effectivequality control test applied to samples ofproduction welds when they can beobtained. However, allowance must bemade for the difference in corrosionresistance of annealed mill products andan as-welded joint. Even a properlymade weld may exhibit a CPT 5 to 15Clower than that of the base metaldepending on the welding procedure,shielding gas and the grade of duplexstainless steel being welded.

6.2.6 Production welding andinspection

The problems that might occur with duplexstainless steel are not readily apparentto the welder, nor are they detectable bynon-destructive testing. The welder mustappreciate that the total quality of theweld, as measured by its toughness andcorrosion resistance in service, dependson strictly following the welding procedure.

Deviations from the qualied procedurewill not necessarily be detectable in theshop, but every deviation represents a riskto safe and economical service.

Bridge in Cala Galdana on Menorca fabricated using 2205 duplex stainless steel. PEDELTA

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7 Mechanical properties

Duplex stainless steels have exceptionalmechanical properties. They are listed forthe standard duplex grades in Table 6.Their room temperature yield strength inthe solution-annealed condition is morethan double that of standard austeniticstainless steels not alloyed with nitrogen.This may allow the design engineer todecrease the wall thickness in someapplications. The typical yield strengths

of several duplex stainless steels arecompared with that of 316L austeniticstainless steel between room temperatureand 300C (570F) in Figure 12.Because of the danger of 475C (885F)embrittlement of the ferritic phase, duplexstainless steels should not be used inservice at temperatures above thoseallowed by the applicable pressure vesseldesign code for prolonged periods oftime (see Table 2).

The mechanical properties of wroughtduplex stainless steels are highly aniso-tropic, that is, they may vary dependingon the orientation of the test sample. Thisanisotropy is caused by the elongatedgrains and the crystallographic texturethat results from hot or cold rolling (seeFigure 2). While the solidication struc-ture of duplex stainless steel is typically

isotropic, it is rolled or forged andsubsequently annealed with both phasespresent. The appearance of the twophases in the nal product reveals thedirectionality of the processing. Thestrength is higher perpendicular to the

rolling direction than in the rolling direction.The impact toughness is higher when thenotch is positioned perpendicular to therolling direction than in the rolling direction.The measured toughness will be higherfor a longitudinal (L-T) Charpy test

ASTM EN

Grade UNS No. Yield strength0.2%

MPa (ksi)

TensilestrengthMPa (ksi)

Elongationin 2

%

EN No. Proofstrength

Rp0.2MPa (ksi)

Tensilestrength

RmMPa (ksi)

ElongationA5%

2304 S32304 400 (58) 600 (87) 25 1.4362 400 (58) 630 (91) 25

2205 S32205 450 (65) 655 (95) 25 1.4462 460 (67) 640 (93) 25

2507 S32750 550 (80) 795 (116) 15 1.4410 530 (77) 730 (106) 20

Table 6: Minimum ASTM and EN mechanical property limits for duplex stainless steel plate

600

2507

2205

2304

316L

S32760

500

400

300

200

100

0

0 50 100 150 200 250 300 350

Yieldstrength(MPa)

Temperature (C)

Figure 12: Comparison of typical yield strength of duplex stainless steels and Type 316L between roomtemperature and 300C (572F). Source: producer data sheets

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specimen than for other test directions.

The impact energy of a transversespecimen from a duplex stainless steelplate will typically be 1/2 to 2/3 that ofa longitudinal specimen.

Despite their high strength, duplex stain-less steels exhibit good ductility andtoughness. Compared with carbon steelor ferritic stainless steels, the ductile-to-brittle transition is more gradual. Duplexstainless steels retain good toughnesseven to low ambient temperatures, forexample, -40C/F; however, ductility and

toughness of duplex stainless steels arein general lower than those of austeniticstainless steels. Austenitic stainless steelstypically do not show a ductile-to-brittle

transition and maintain excellent tough-

ness down to cryogenic temperatures. Acomparison of minimum elongation inthe tensile test for the standard austeniticand the duplex stainless steels is givenin Table 7.

While the high yield strength of duplexstainless steel can allow down gauging,depending on buckling and YoungsModulus limitations, it can also posechallenges during fabrication. Because ofthe higher strength of duplex stainlesssteels, higher forces are required to

deform them. As a result, their springbackin bending operations is larger than thatof austenitic stainless steels. A spring-back comparison of two duplex stainless

ASTM A 240 EN 10088-2

Grade UNS No. Elongation, min. (%) EN No. Elongation, min. (%)*

P H C

S32101 30 1.4162

S32202 30 1.4062

2304 S32304 25 1.4362 25 20 20

S32003 25

2205 S32205 25 1.4462 25 25 20

2507 S32750 15 1.4410 20 15 15

304L S30403 40 1.4307 45 45 45

316L S31603 40 1.4404 45 40 40

Table 7: Comparison of the ductility of duplex and austenit ic stainless steels according to the requirements of ASTM A 240 and EN 10088-2.

Installation of insulated 24 inch 2205 pipe onvertical support members in Prudhoe Bay. Arco Exploration and Product ion Technology

P = hot rolled plate H = hot rolled coil C = cold rolled coil and sheet * transverse direction


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steels and Type 316L austenitic stainlesssteel is shown in Figure 13. Duplexstainless steels have less ductility than

austenitic stainless steels and increasedbend radii may be required to avoidcracking.

Because of their higher hardness andthe high work hardening rate, duplexstainless steels typically reduce tool lifein machining operations or increasemachining times compared with standardaustenitic grades. Annealing cycles maybe needed between forming or bendingoperations because the ductility of duplex

stainless steels is approximately halfthat of the austenitic stainless steels. Theeffect of cold work on the mechanicalproperties of 2205 is shown in Figure 14.

110

2205

2304316L

100

50

40

30

20

90

80

70

60

10

30 40 50 60 70 80 90 100 110 120

Bending angle (degrees)

Finalbendangle(degrees)

Figure 13: Comparison of springback of duplex stainless steels and Type 316L for 2 mm (0.08 inch) thicksheet. Source: Outokumpu

1400

Tensile strength

0.2% offset yield strength

HV

Elongation

1300

800

700

600

1200

1100

1000

900

600

550

300

250

500

450

400

350

32

28

8

4

0

24

20

16

12

30

26

6

2

22

18

14

10

0 10 20 30 40 50 60 70 9080

Cold work (%)

Stress(N

/mm2)

Elongation(%)

HV

Figure 14: Effect of cold work on the mechanical properties of 2205 duplex stainless steel. Source: Baosteel


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8 Physical properties

Ambient-temperature physical propertiesfor a selection of duplex stainless steelsare given in Table 8, and selected elevatedtemperature values are given in Table 9.Data are included for carbon steel andaustenitic stainless steels for comparison.

In all cases, differences in physicalproperty values among the duplex gradesare very slight and probably reectdifferences in test procedures. The physi-cal properties of the duplex grades allfall between those of austenitic stainless

steels and carbon steels, but tend tobe closer to those of the stainless steels.

Grade UNS No. Density Specific heat Electrical resistivity Youngs modulus

g/cm3 lb./in3 J/kg K Btu/lb./F micro m micro in. GPa x10 6 psi

Carbon steel G10200 7.64 0.278 447 0.107 0.10 3.9 207 30.0

Type 304 S30400 7.98 0.290 502 0.120 0.73 28.7 193 28.0

Type 316 S31600 7.98 0.290 502 0.120 0.75 29.5 193 28.0

Type 329 S32900 7.75 0.280 460 0.110 0.80 31.5 200 29.0

S32101 7.80 0.281 500 0.119 0.80 31.5 200 29.0

2304 S32304 7.75 0.280 482 0.115 0.80 31.5 200 29.0

S31803 7.80 0.281 500 0.119 0.80 31.5 200 29.0

2205 S32205 7.80 0.281 500 0.119 0.80 31.5 200 29.0

S31260 7.80 0.281 502 0.120 200 29.0

255 S32550 7.82 0.282 488 0.116 0.84 33.1 210 30.5

S39274 7.80 0.281 502 0.120 200 29.0

S32520 7.75 0.280 450 0.108 0.85 33.5 205 29.7

2507 S32750 7.75 0.280 485 0.115 0.80 31.5 200 29.0

S32760 7.80 0.281 0.85 33.5 190 27.6

S32707 7.80 0.281 470 0.112 0.75 29.5 197 28.5

Table 8: Ambient temperature physical properties of duplex stainless steels compared with carbon steel and austenitic stainless steels.

Source: producer data sheets


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Table 9: Elevated temperature physical properties of duplex stainless steels compared with carbon steel and austenitic stainless steels.Source: producer data sheets

Grade UNS No. 20C (68F) 100C (212F) 200C (392F) 300C (572F) 400C (754F) 500C (932F)

Elastic modulus in tension as a function of temperature in units of GPa (ksi x 1,000)

Carbon steel G10200 207 (30.0)

Type 304 S30400 193 (28.0) 192 (27.9) 183 (26.6) 177 (25.7) 168 (24.4) 159 (23.0)

Type 329 S32900 200 (29.0) 195 (28.0) 185 (27.0)

S32101 200 (29.0) 194 (28.0) 186 (27.0) 180 (26.1

2304 S32304 200 (29.0) 190 (27.6) 180 (26.1) 170 (24.7) 160 (23.2) 150 (21.8)

S31803 200 (29.0) 190 (27.6) 180 (26.1) 170 (24.7) 160 (23.2) 150 (21.8)

2205 S32205 200 (29.0) 190 (27.6) 180 (26.1) 170 (24.7) 160 (23.2) 150 (21.8)255 S32550 210 (30.5) 200 (29.9) 198 (28.7) 192 (27.8) 182 (26.4) 170 (24.7)

S32520 205 (29.7) 185 (26.8) 185 (26.8) 170 (24.7)

2507 S32750 200 (29.0) 190 (27.6) 180 (26.1) 170 (24.7) 160 (23.2) 150 (21.8)

S32707 197 (28.5) 189 (27.5) 178 (25.7) 168 (24.2)

Coefficient of thermal expansion from 20C (68F) to T in units of 10-6/K (10-6/F)

Carbon steel G10200 NA 12.1 (6.70) 13.0 (7.22) 14 (7.78)

Type 304 S30400 NA 16.4 (9.10) 16.9 (9.40) 17.3 (9.60) 17.6 (9.80) 18.0 (10.0)

Type 329 S32900 NA 10.9 (6.10) 11.0 (6.30) 11.6 (6.40) 12.1 (6.70) 12.3 (6.80)

S32101 NA 13.0 (7.22) 13.5 (7.50) 14.0 (7.78)

2304 S32304 NA 13.0 (7.22) 13.5 (7.50) 14.0 (7.78) 14.5 (8.06) 15.0 (8.33)

S31803 NA 13.0 (7.22) 13.5 (7.50) 14.0 (7.78) 14.5 (8.06) 15.0 (8.33)

2205 S32205 NA 13.0 (7.22) 13.5 (7.50) 14.0 (7.78) 14.5 (8.06) 15.0 (8.33)

255 S32550 NA 12.1 (6.72) 12.6 (7.00) 13.0 (7.22) 13.3 (7.39) 13.6 (7.56)

S32520 NA 12.5 (6.94) 13.0 (7.22) 13.5 (7.50)

2507 S32750 NA 13.0 (7.22) 13.5 (7.50) 14.0 (7.78) 14.5 (8.06) 15.0 (8.33)

S32707 NA 12.5 (6.94) 12.5 (6.94) 13.0 (7.22) 13.5 (7.50) 14.0 (7.78)

Thermal conductivity as a function of temperature in units of W/m K (Btu in/hr ft 2 F)

Carbon steel G10200 52 (360) 51 (354) 49 (340) 43 (298)

Type 304 S30400 14.5 (100) 16.2 (112) 17.8 (123) 19.6 (135) 20.3 (140) 22.5 (155)

S32101 15.0 (105) 16.0 (110) 17.0 (118) 18.0 (124)

2304 S32304 16.0 (110) 17.0 (118) 19.0 (132) 20.0 (138) 21.0 (147) 22.0 (153)

S31803 16.0 (110) 17.0 (118) 19.0 (132) 20.0 (138) 21.0 (147) 22.0 (153)

2205 S32205 16.0 (110) 17.0 (118) 19.0 (132) 20.0 (138) 21.0 (147) 22.0 (153)

255 S32550 14.3 (98.5) 16.4 (113) 18.6 (128) 19.1 (133) 20.9 (145) 22.5 (156)

S32520 17.0 (118) 18.0 (124) 19.0 (132) 20.0 (138)

2507 S32750 16.0 (110) 17.0 (118) 19.0 (132) 20.0 (138) 21.0 (147) 22.0 (153)

S32707 12.0 (84) 14.0 (96) 16.0 (110) 18.0 (124) 19.0 (132)


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9 Cutting

The same processes typically appliedto austenitic stainless steels and tocarbon steels may be used to cut duplexstainless steels, but some adjustmentsin parameters will be necessary to accom-modate the differences in mechanicalproperties and thermal response.

9.1 Sawing

Because of their high strength, high workhardening rate, and the virtual absenceof inclusions that would serve as chip-breakers, duplex stainless steels are moredifficult to saw than carbon steels.Best results are achieved with powerfulmachines, strong blade alignmentsystems, coarse-toothed blades, slow-to-moderate cutting speeds, heavy feeds,and a generous ow of coolant, ideally asynthetic emulsion which provides lubrica-tion as well as cooling, delivered so

that the blade carries the coolant into theworkpiece. The cutting speeds andfeeds should be similar to those used forType 316 austenitic stainless steel.

9.2 Shearing

Duplex stainless steels are sheared onthe same equipment used to shear Types304 and 316, usually with no specialadjustments. However, because of thegreater shear strength of the duplexstainless steels, the power of the shear

must be greater or the sheared thicknessreduced.

The shear strength of stainless steelsis about 58% of the ultimate tensilestrength for both hot rolled plate and forcold rolled sheet. Duplex stainless steelsbehave the same as would be expectedof a thicker piece of Type 316 stainlesssteel. Therefore, the maximum thicknessof 2304 or 2205 duplex stainless steel

that can be cut on a particular shear isabout 75% of that for Type 304 or 316.The maximum thickness of super duplexstainless steels that can be cut on a par-ticular shear is about 65% of the commonaustenitic grades.

9.3 Slitting

Conventional coil slitters are used toshear coiled duplex stainless steel sheet

or strip. The coiled stainless steel feedsoff from a payoff reel and through anupper and lower arbor on the slitting linethat contains circular slitting knives, anda take-up reel recoils the slit width coils.The position of the slitting knives can beadjusted based on the desired slit multwidth of the coil product. Because of thehigher strength of duplex stainless steelscompared to austenitic stainless steels,slitter knife tool wear and slit edge

consistency are more difficult to control.Maintaining good slit edge quality ofduplex stainless steel coils requires theuse of tool steel or carbide slitter knifes.

9.4 Punching

Punching may be viewed as a difficultform of shearing. The high strength, rapidwork hardening, and resistance to tearing

make duplex stainless steels relativelydifficult to punch and abrasive to thetooling. A good starting point and guide-line is to assume that duplex stainlesssteel will behave similarly to an austeniticstainless steel twice its thickness. Themore highly alloyed duplex stainlesssteels with higher levels of nitrogen aredisproportionately more difficult.

9.5 Plasma and laser cutting

Duplex stainless steels are routinelyprocessed with the same plasma cuttingand laser cutting equipment used forprocessing austenitic stainless steels. Theslightly higher thermal conductivity andthe typically low sulfur content in duplexstainless steels may affect the optimalparameters marginally, but acceptableresults can be achieved without specialadjustment. The HAZ of the plasmacutting process is typically narrow, about0.25 mm (0.010 inch) because the cutis made rapidly in one pass with rapid

cooling from the plate or sheet. The normalmachining of a weld preparation andthe melting of adjacent base metal duringwelding will remove the HAZ of the plasmacutting process.

Slitting of duplex stainless steel. Outokumpu


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10 Forming

10.1 Hot-forming

Duplex stainless steels show excellenthot formability with relatively low formingloads up to at least 1230C (2250F).However, if hot-forming takes place attoo low a temperature, deformationaccumulates in the weaker but lessductile ferrite, which can result in crackingof the ferrite in the deformed region.

Additionally, a large amount of sigmaphase can be precipitated when the hot-working temperature drops too low.

Most producers recommend a maximumhot-forming temperature between 1100C(2000F) and 1150C (2100F). Thisupper temperature limit is suggestedbecause of the effect of high temperatureson the dimensional stability of a partand the increased tendency to formscale above 1150C (2100F). At thesetemperatures, duplex stainless steelbecomes soft and fabricated pieces suchas vessel heads or piping warp or sag

in the furnace if they are not supported.At these temperatures the steel may alsobecome too soft for certain hot-formingoperations. Table 10 summarizes thesuggested temperature ranges for hot-forming and the minimum soakingtemperatures. It is not necessary or alwaysadvisable, to start hot-working at thehighest temperature in the range. How-ever, the steel should reach at leastthe minimum soaking temperature beforehot-working. The furnace should becharged hot, to avoid slow heating throughthe temperature range where sigma phaseis formed.

Temperature uniformity is important insuccessful hot-forming of duplex stainlesssteel. If the shape of the workpiece is not

compact, the edges may be signicantlycooler than the bulk, and there is arisk of cracking in these cooler regions.

To avoid this cracking, it is necessary toreheat the piece when these localregions are in danger of cooling below theminimum hot-working temperature. Thelower end of the suggested hot-formingtemperature range may be extendedsomewhat, but only if the temperatureuniformity within the workpiece, especiallythe edges or thinner sections, is main-tained.

With heavy sections, it is appropriate

to consider whether water quenching isfast enough to prevent precipitation ofi

Documents

Duplex Stainless Steel 3rd Edition (1)